Effect of Rare Earth on Microstructure and Wear Resistance of In-Situ-Synthesized Mo2FeB2 Ceramics-Reinforced Fe-Based Cladding

Mo2FeB2 ceramics-reinforced Fe-based cladding with various rare earth (RE) concentrations were prepared by the carbon arc surfacing process. The effects of RE content on the microstructure, phase composition, hardness and wear resistance of the cladding were systematically discussed. Meanwhile, the area fraction and grain size of Mo2FeB2 phase were exactly measured. Moreover, the refining mechanism of rare earth Y was analyzed. Results revealed that the claddings consisted of Mo2FeB2, FeCr, MoB and CrB. Adding the rare-earth Y decreased the grain sizes of Mo2FeB2 phase. Furthermore, grain-refining effects of Mo2FeB2 phase were significant when the RE content was 2% and hard phases evenly distributed in the cladding. In addition, the maximum microhardness value of claddings was about 1078 HV. The claddings with 2% RE contents had better wear resistance, which was equivalent to a sintered sample.

In general, Mo 2 FeB 2 -based cermets are synthesized by reactive boronization sintering, Yu et al. [10,11] have obtained Mo 2 FeB 2 -based cermets using the sintering process and pointed out that sintering temperature can influence the morphology of the Mo 2 FeB 2 phase. In addition, the effect of alloying elements on their densification behavior, microstructure and properties have been systematically investigated [12][13][14][15]. However, it is worth mentioning that expensive equipment and complex processes would increase costs and limit applications of Mo 2 FeB 2 -based cermet. At the same time, the preparation of Mo 2 FeB 2 -based claddings using welding techniques has rarely been studied. Welding has its own advantages such as simple operation and low costs contrasted with the sintering process. However, Mo 2 FeB 2 growing from weld pool makes Mo 2 FeB 2 have a large size and many problems such as insufficient hardness, large brittleness and poor wear resistance.
Rare earth (RE) elements have the ability to reduce the effect of impurity by forming intermetallic compounds and purify the melt [16]. In addition, RE elements can reduce the amount of second phases and grain size, resulting in a more homogeneous and refined microstructure [17]. Wang et al. [18]  Alloy blocks was placed on the surface of Q235 steel substrate using ZX7-400 STG carbon arc welding machine (Shandong Aotai Electric Co., Ltd., Jinan, China). A graphite rod was held with a welding torch so that an arc was formed between the graphite rod and the substrate. The alloy block melted into the weld pool formed on the substrate, thereby reducing the burning loss of the alloy elements. The technological parameters of the surfacing process given in Table 3. After that, the second layer was fabricated with the same optimized parameters. Figure 1 illustrates schematic diagram of the carbon arc surfacing.   After welding, the cladding was cut into a typical cross section. Then, the samples were ground with abrasive papers and polished by 1.5 μm diamond paste before observation. Subsequently, the specimens were etched using a mixed acid solution (HF: 20 vol.%, HCL: 30 vol.%, HNO3: 50 vol.%) within 12~14 s. The microstructure was studied with scanning electron microscope (SEM) (JSM-6600V, Japanese electronics company, Tokyo, Japan) in backscattered electron (BSE) mode. While analysis of the chemical composition of both the hard-phase and eutectic matrix was performed by energy dispersive spectroscopy (EDS) linked to SEM, X-ray diffraction (XRD) line profiles were measured using an x-ray diffractometer with Cu Kα radiation (λ = 0.154056 nm) and the scanning rate was set as 8°/min with a scan step of 0.02°. Phase fraction and grain size were measured by Image-Pro Plus 6.0 (IPP 6.0) software (National Institutes of Health, Bethesda, America). In addition, electron probe micro-analysis (EPMA-JXA-8530F PLUS, Japanese electronics company, Tokyo, Japan) was employed to investigate the existence and distribution of rare-earth Ce, Y elements in the Mo2FeB2 claddings.
Microhardness along the depth in cross-sections of claddings was measured using micro-Vickers hardness tester (DHV-1000, Shanghai Shangcai Testing Machine Co., Ltd., Shanghai, China) with a load of 500 g for 10 s dwell time. The wear resistance test was conducted on M-2000 testing machine (Hebei Xuanhua Zhengli Balancing Machine Co., Ltd., Hebei, China) by a block on ring wear tester under dry and rotating conditions in room temperature. The samples were machined to 31 mm × 7 mm × 5 mm by wire-cut electrical discharge machining (EDM) (DK7732, Taizhou Tianlong CNC Machine Tool Co., Ltd., Taizhou, China). Then, the samples were ground with abrasive papers to remove metallic oxide off the surface, which smoothed the sample surface. Carburized 20CrMnTi steel with the size of 40 mm in diameter and 10 mm in thickness was employed as the counterpart, which had a Rockwell hardness of 60.2 HRC. The load, the rotating speed and wear time were 1.5 × 10 2 N, 4.0 × 10 2 r/min and 60 min, respectively. As comparison, Mo2FeB2-sintered samples were also given a wear-resistance test under the same conditions. The wear weight-loss value of the specimens was calculated by averaging three measurements. Before the weight-loss measurements, samples were washed with ultrasonic cleaning apparatus and dried. Alongside, the wear morphology of the claddings and sintered samples were observed by SEM. After welding, the cladding was cut into a typical cross section. Then, the samples were ground with abrasive papers and polished by 1.5 µm diamond paste before observation. Subsequently, the specimens were etched using a mixed acid solution (HF: 20 vol.%, HCL: 30 vol.%, HNO 3 : 50 vol.%) within 12~14 s. The microstructure was studied with scanning electron microscope (SEM) (JSM-6600V, Japanese electronics company, Tokyo, Japan) in backscattered electron (BSE) mode. While analysis of the chemical composition of both the hard-phase and eutectic matrix was performed by energy dispersive spectroscopy (EDS) linked to SEM, X-ray diffraction (XRD) line profiles were measured using an x-ray diffractometer with Cu Kα radiation (λ = 0.154056 nm) and the scanning rate was set as 8 • /min with a scan step of 0.02 • . Phase fraction and grain size were measured by Image-Pro Plus 6.0 (IPP 6.0) software (National Institutes of Health, Bethesda, America). In addition, electron probe micro-analysis (EPMA-JXA-8530F PLUS, Japanese electronics company, Tokyo, Japan) was employed to investigate the existence and distribution of rare-earth Ce, Y elements in the Mo 2 FeB 2 claddings.

Microstructure and Composition
Microhardness along the depth in cross-sections of claddings was measured using micro-Vickers hardness tester (DHV-1000, Shanghai Shangcai Testing Machine Co., Ltd., Shanghai, China) with a load of 500 g for 10 s dwell time. The wear resistance test was conducted on M-2000 testing machine (Hebei Xuanhua Zhengli Balancing Machine Co., Ltd., Hebei, China) by a block on ring wear tester under dry and rotating conditions in room temperature. The samples were machined to 31 mm × 7 mm × 5 mm by wire-cut electrical discharge machining (EDM) (DK7732, Taizhou Tianlong CNC Machine Tool Co., Ltd., Taizhou, China). Then, the samples were ground with abrasive papers to remove metallic oxide off the surface, which smoothed the sample surface. Carburized 20CrMnTi steel with the size of 40 mm in diameter and 10 mm in thickness was employed as the counterpart, which had a Rockwell hardness of 60.2 HRC. The load, the rotating speed and wear time were 1.5 × 10 2 N, 4.0 × 10 2 r/min and 60 min, respectively. As comparison, Mo 2 FeB 2 -sintered samples were also given a wear-resistance test under the same conditions. The wear weight-loss value of the specimens was calculated by averaging three measurements. Before the weight-loss measurements, samples were washed with ultrasonic cleaning apparatus and dried. Alongside, the wear morphology of the claddings and sintered samples were observed by SEM.   Figure 3 shows the typical microstructure with different RE contents. The cladding is mainly composed of white hard phases and eutectic structure and the RE content has distinct influence on the microstructure of claddings. The number of white hard phases of cladding with RE contents remarkably increases compared with the cladding without RE content. Moreover, the hard phases in cladding are significantly refined when the RE content is 2%. As the RE contents increase, the hard phases begin to grow coarse. When the RE content arrives at 8%, the hard phases are so coarse that some of them connect to each other. This is because the nucleation rate of the system will increase as the content of rare-earth elements increases [23]. At the same time, according to the dissolution and diffusion mechanism [24], small hard-phase particles dissolve during the arc thermal cycle and Mo and B precipitate on the originally coarse Mo2FeB2 hard particles, which serve as nucleation centers and gradually grow to connect to each other. Moreover, the composition of hard phase and eutectic structure of the cladding with 2% RE content were analyzed by EDS. The results of EDS are listed in Table 4. It should be noted that the B content were not accurate because of the insensitivity of EDS to B element. Point 1 and point 2 in Figure 3b are used for spot scans of the hard phases and eutectic structure, respectively. From Table 4, it was found that there was Mo, Fe, Cr and B in the hard phase and eutectic structure. However, it obviously showed that Mo content was enriched in white hard phases, and Fe content was concentrated in the eutectic structure. Combining with XRD and EDS results, the white hard phases are Mo2FeB2 and M3B2 complex boride type.  Figure 3 shows the typical microstructure with different RE contents. The cladding is mainly composed of white hard phases and eutectic structure and the RE content has distinct influence on the microstructure of claddings. The number of white hard phases of cladding with RE contents remarkably increases compared with the cladding without RE content. Moreover, the hard phases in cladding are significantly refined when the RE content is 2%. As the RE contents increase, the hard phases begin to grow coarse. When the RE content arrives at 8%, the hard phases are so coarse that some of them connect to each other. This is because the nucleation rate of the system will increase as the content of rare-earth elements increases [23]. At the same time, according to the dissolution and diffusion mechanism [24], small hard-phase particles dissolve during the arc thermal cycle and Mo and B precipitate on the originally coarse Mo 2 FeB 2 hard particles, which serve as nucleation centers and gradually grow to connect to each other. Moreover, the composition of hard phase and eutectic structure of the cladding with 2% RE content were analyzed by EDS. The results of EDS are listed in Table 4. It should be noted that the B content were not accurate because of the insensitivity of EDS to B element. Point 1 and point 2 in Figure 3b are used for spot scans of the hard phases and eutectic structure, respectively. From Table 4, it was found that there was Mo, Fe, Cr and B in the hard phase and eutectic structure. However, it obviously showed that Mo content was enriched in white hard phases, and Fe content was concentrated in the eutectic structure. Combining with XRD and EDS results, the white hard phases are Mo 2 FeB 2 and M 3 B 2 complex boride type.  To further analyze the formation mechanism of Mo2FeB2 hard phase in claddings, CALPHAD modelling of multicomponent Mo-Fe-B systems was employed using Pandat software (Pandat 2020, CnTech Company, Beijing, China) [25]. The Cr compounds were not considered. The SGTE thermodynamic database was used for alloy systems [26]. Figure 4 shows the calculated liquidus surface projection of Mo-Fe-B system and Molar fraction variation of each phase. From Figure 4b, the MoB phase precipitates from the liquid phase at 1820 °C (L→MoB). At 1491 °C, the molar fraction of the liquid phase decreases sharply and the MoB phase of that continues growing. The molar fraction of the Mo2FeB2 phase starts to increase, which illustrates that the Mo2FeB2 phase begins to precipitate. It should be noted that Mo2FeB2 phase has two types of forming methods. Firstly, the Mo2FeB2 phase precipitates from the liquid phase (L→Mo2FeB2) [27]. Secondly, MoB reacts with Fe to form the Mo2FeB2 phase (2MoB+Fe→Mo2FeB2) [28]. Therefore, the Mo2FeB2 phase could form according to these methods at 1491 °C. As temperature decreases, the liquid phase diminishes until it disappears at 1442 °C. In this temperature range, the liquid phase, the MoB phase and the Mo2FeB2 phase can coexist. In addition, Wang et al. [27] calculated the variation of Gibbs free energy of Mo-Fe-B-Cr system in the weld pool at 1389 °C and pointed out that the Gibbs free energy of MoB and CrB were −136 KJ/mol and −59.581 KJ/mol, respectively, illustrating that MoB and CrB phases can exist in high temperature, liquid phase, which was consistent with the XRD results ( Figure 2).  To further analyze the formation mechanism of Mo 2 FeB 2 hard phase in claddings, CALPHAD modelling of multicomponent Mo-Fe-B systems was employed using Pandat software (Pandat 2020, CnTech Company, Beijing, China) [25]. The Cr compounds were not considered. The SGTE thermodynamic database was used for alloy systems [26]. Figure 4 shows the calculated liquidus surface projection of Mo-Fe-B system and Molar fraction variation of each phase. From Figure 4b, the MoB phase precipitates from the liquid phase at 1820 • C (L→MoB). At 1491 • C, the molar fraction of the liquid phase decreases sharply and the MoB phase of that continues growing. The molar fraction of the Mo 2 FeB 2 phase starts to increase, which illustrates that the Mo 2 FeB 2 phase begins to precipitate. It should be noted that Mo 2 FeB 2 phase has two types of forming methods. Firstly, the Mo 2 FeB 2 phase precipitates from the liquid phase (L→Mo 2 FeB 2 ) [27]. Secondly, MoB reacts with Fe to form the Mo 2 FeB 2 phase (2MoB+Fe→Mo 2 FeB 2 ) [28]. Therefore, the Mo 2 FeB 2 phase could form according to these methods at 1491 • C. As temperature decreases, the liquid phase diminishes until it disappears at 1442 • C. In this temperature range, the liquid phase, the MoB phase and the Mo 2 FeB 2 phase can coexist. In addition, Wang et al. [27] calculated the variation of Gibbs free energy of Mo-Fe-B-Cr system in the weld pool at 1389 • C and pointed out that the Gibbs free energy of MoB and CrB were −136 KJ/mol and −59.581 KJ/mol, respectively, illustrating that MoB and CrB phases can exist in high temperature, liquid phase, which was consistent with the XRD results ( Figure 2).

Statistics of Phase Fraction and Grain Size
As for the statistics of phase fraction and grain size, 20 images of each sample were used for the determination and here we just chose the most representative images to show. Figure 5 shows the images of hard-phase fraction. The light color indicates the Mo2FeB2 phase while the dark color belongs to the matrix phase. When the RE content is 0%, 2%, 4% and 8%, the area fraction of Mo2FeB2 hard phase is 59%, 72%, 67% and 74%, respectively. The addition of rare-earth elements increases the amount of Mo2FeB2 hard phase, so that the area fraction of Mo2FeB2 hard phase in the cladding with RE content is as high as 67% or more. Moreover, when the RE content is 2% (Figure 5b), the Mo2FeB2 phase is refined and area fraction reaches 72%, which is 14% higher than the cladding with 0% RE content. Figure 6 shows grain size distribution of Mo2FeB2 hard phases with different RE contents. When

Statistics of Phase Fraction and Grain Size
As for the statistics of phase fraction and grain size, 20 images of each sample were used for the determination and here we just chose the most representative images to show. Figure 5 shows the images of hard-phase fraction. The light color indicates the Mo 2 FeB 2 phase while the dark color belongs to the matrix phase. When the RE content is 0%, 2%, 4% and 8%, the area fraction of Mo 2 FeB 2 hard phase is 59%, 72%, 67% and 74%, respectively. The addition of rare-earth elements increases the amount of Mo 2 FeB 2 hard phase, so that the area fraction of Mo 2 FeB 2 hard phase in the cladding with RE content is as high as 67% or more. Moreover, when the RE content is 2% (Figure 5b), the Mo 2 FeB 2 phase is refined and area fraction reaches 72%, which is 14% higher than the cladding with 0% RE content.

Statistics of Phase Fraction and Grain Size
As for the statistics of phase fraction and grain size, 20 images of each sample were used for the determination and here we just chose the most representative images to show. Figure 5 shows the images of hard-phase fraction. The light color indicates the Mo2FeB2 phase while the dark color belongs to the matrix phase. When the RE content is 0%, 2%, 4% and 8%, the area fraction of Mo2FeB2 hard phase is 59%, 72%, 67% and 74%, respectively. The addition of rare-earth elements increases the amount of Mo2FeB2 hard phase, so that the area fraction of Mo2FeB2 hard phase in the cladding with RE content is as high as 67% or more. Moreover, when the RE content is 2% (Figure 5b), the Mo2FeB2 phase is refined and area fraction reaches 72%, which is 14% higher than the cladding with 0% RE content.    Figure 6 shows grain size distribution of Mo 2 FeB 2 hard phases with different RE contents. When the RE content is 0%, average grain size of the Mo 2 FeB 2 hard phase is 16.52 µm and mainly distributed in 14~25 µm, as shown in Figure 6a. In terms of 2% RE content, average grain size of the Mo 2 FeB 2 hard phase is 4.78 µm and primarily distributed in 4.2~5.2 µm (Figure 6b). When the RE content is 4%, average grain size of the Mo 2 FeB 2 hard phase is 8.2 µm and principally distributed in 6~8 µm, as shown in Figure 6c. As for 8% RE content, average grain size of the Mo 2 FeB 2 hard phase is 8.88 µm and chiefly distributed in 6~9 µm (Figure 6d).
Materials 2020, 13, x FOR PEER REVIEW 7 of 15 the RE content is 0%, average grain size of the Mo2FeB2 hard phase is 16.52 μm and mainly distributed in 14~25 μm, as shown in Figure 6a. In terms of 2% RE content, average grain size of the Mo2FeB2 hard phase is 4.78 μm and primarily distributed in 4.2~5.2 μm (Figure 6b). When the RE content is 4%, average grain size of the Mo2FeB2 hard phase is 8.2 μm and principally distributed in 6~8 μm, as shown in Figure 6c. As for 8% RE content, average grain size of the Mo2FeB2 hard phase is 8.88 μm and chiefly distributed in 6~9 μm (Figure 6d).  Figure 7 shows the effect of RE content on grain size and size variance of the Mo2FeB2 hard phases. From Figure 7, the average grain size of the Mo2FeB2 hard phases is significantly refined and the size variance is smaller with adding RE. When the RE content is 2%, the size of the Mo2FeB2 hard phases is 1/3.44 of the cladding with 0% RE content, the smallest variance, which is the best addition for the refinement.   Figure 7 shows the effect of RE content on grain size and size variance of the Mo 2 FeB 2 hard phases. From Figure 7, the average grain size of the Mo 2 FeB 2 hard phases is significantly refined and the size variance is smaller with adding RE. When the RE content is 2%, the size of the Mo 2 FeB 2 hard phases is 1/3.44 of the cladding with 0% RE content, the smallest variance, which is the best addition for the refinement. the RE content is 0%, average grain size of the Mo2FeB2 hard phase is 16.52 μm and mainly distributed in 14~25 μm, as shown in Figure 6a. In terms of 2% RE content, average grain size of the Mo2FeB2 hard phase is 4.78 μm and primarily distributed in 4.2~5.2 μm (Figure 6b). When the RE content is 4%, average grain size of the Mo2FeB2 hard phase is 8.2 μm and principally distributed in 6~8 μm, as shown in Figure 6c. As for 8% RE content, average grain size of the Mo2FeB2 hard phase is 8.88 μm and chiefly distributed in 6~9 μm (Figure 6d).  Figure 7 shows the effect of RE content on grain size and size variance of the Mo2FeB2 hard phases. From Figure 7, the average grain size of the Mo2FeB2 hard phases is significantly refined and the size variance is smaller with adding RE. When the RE content is 2%, the size of the Mo2FeB2 hard phases is 1/3.44 of the cladding with 0% RE content, the smallest variance, which is the best addition for the refinement.

Refining Mechanism of Rare Earth
To further study the mechanism of RE content on Mo 2 FeB 2 hard phases, the electronic probe (EPMA) was employed to analyze element distribution of samples. Figure 8 presents the elements' distribution of cladding with 0% and 2% RE contents. Mo and B elements are mainly enriched in Mo 2 FeB 2 hard phases, as shown in Figure 8a2 Figure 8b4-Fe), and Cr element is principally concentrated in the matrix, which guarantees that the matrix has certain corrosion resistance [12]. Figure 8b6-Ce and Figure 8b7-Y are the distribution images of the Ce and Y elements. The distribution of Ce element is relatively uniform and there is no obvious segregation phenomenon, while the Y element is enriched in Mo 2 FeB 2 hard phases. Elemental Y has higher melting point (1522 • C)-Liu [29] found that Y can be used as the nucleation particle of Mg 2 Si and refining the grains of Mg 2 Si. The Y element is segregated in the Mo 2 FeB 2 hard phases (Figure 8b7-Y), which can be used as potential hard-nucleation particle of the Mo 2 FeB 2 phase and increase the number of Mo 2 FeB 2 phases as well as refining the grains of the Mo 2 FeB 2 phase. In addition, according to the solidification theory, nucleation work ∆G and nucleation rate N can be obtained by Equations (1) and (2) [30].
where, σ LS represents solid-liquid interfacial tension; ∆G m is the solid-liquid unit volume free energy difference; k is the boltzmann constant; N 0 is constant and T is temperature of the liquid metal, respectively. The addition of Ce, Y active elements reduce solid-liquid interfacial tension (σ LS ). According to Equation (1), the nucleation work ∆G also decreases. Therefore, more and more liquid atoms reach the nucleation work through energy fluctuations, which improves the nucleation rate N according to Equation (2). In addition, during solidification of weld pool, rare-earth Y is enriched in the front of the solid-liquid interface due to the limitation of diffusion [31], the inter metallic compounds with high points containing rare-earth Y are dispersed at grain boundaries [31], which hinders the growth of the Mo 2 FeB 2 nucleus and refines the Mo 2 FeB 2 grain size. At the same time, Ce, Y active elements increase the fluidity of the liquid metal [32] and reduce the component supercooling during solidification as well as decrease the component segregation [33] to homogenize the structure. Figure 9 shows the schematic diagram of rare-earth action mechanism. In Figure 9a, according to previous analysis, the Mo 2 FeB 2 nucleus forms according to two types of forming methods (L→Mo 2 FeB 2 , 2MoB + Fe→Mo 2 FeB 2 ). Meanwhile, rare-earth Y rapidly diffuses around the Mo 2 FeB 2 particles, as shown in Figure 9b, where a hard-phase nucleus grows. Y, surface active element, acts as a surface-active film formed on the interface of solid and liquid and also hinders the diffusion of Mo, Fe and B atoms in the liquid metal to the Mo 2 FeB 2 nucleus (Figure 9c). Thus, the growth of Mo 2 FeB 2 grains is restricted. In addition, Y reduces solid-liquid interfacial tension (σ LS ) and decreases the specific surface energy. Mo atoms, B atoms and Fe atoms are enriched in the surface of the nucleus with Y and the Mo 2 FeB 2 nucleus precipitated from liquid is also enriched in the surface, as shown in Figure 9d. In Figure 9e, MoB react with Fe to form Mo 2 FeB 2 particles when the composition, energy and structure requirements are met, the newly grown Mo 2 FeB 2 surface is enriched in the active film containing Y again and the growth of Mo 2 FeB 2 grains is restricted. Repeating this process, the Mo 2 FeB 2 hard phase grows until the liquid metal cools to the eutectic temperature, as shown in Figure 9h. At last, all the remaining liquid phase is converted to Mo 2 FeB 2 , MoB, CrB and FeCr matrix, as shown in Figure 9i.
where, σ represents solid-liquid interfacial tension; ΔGm is the solid-liquid unit volume free energy difference; k is the boltzmann constant; N0 is constant and T is temperature of the liquid metal, respectively. The addition of Ce, Y active elements reduce solid-liquid interfacial tension (σLS). According to Equation (1), the nucleation work ΔG also decreases. Therefore, more and more liquid atoms reach the nucleation work through energy fluctuations, which improves the nucleation rate N according to Equation (2). In addition, during solidification of weld pool, rare-earth Y is enriched in the front of the solid-liquid interface due to the limitation of diffusion [31], the inter metallic compounds with high points containing rare-earth Y are dispersed at grain boundaries [31], which hinders the growth of the Mo2FeB2 nucleus and refines the Mo2FeB2 grain size. At the same time, Ce, Y active elements increase the fluidity of the liquid metal [32] and reduce the component supercooling during solidification as well as decrease the component segregation [33] to homogenize the structure. Figure 9 shows the schematic diagram of rare-earth action mechanism. In Figure 9a, according to previous analysis, the Mo2FeB2 nucleus forms according to two types of forming methods (L→ Mo2FeB2, 2MoB + Fe→Mo2FeB2). Meanwhile, rare-earth Y rapidly diffuses around the Mo2FeB2 particles, as shown in Figure 9b, where a hard-phase nucleus grows. Y, surface active element, acts  Figure 10 shows average microhardness from substrate to the claddings. The average microhardness of the claddings with 0%, 2%, 4% and 8% RE are about 992 ± 59 HV, 1078 ± 105 HV, 929 ± 165 HV and 743 ± 100 HV, respectively, which is 4~6 times that of the substrate (180 HV), and the average microhardness of sintered samples is 925.5 HV.  Figure 10 shows average microhardness from substrate to the claddings. The average microhardness of the claddings with 0%, 2%, 4% and 8% RE are about 992 ± 59 HV, 1078 ± 105 HV, 929 ± 165 HV and 743 ± 100 HV, respectively, which is 4~6 times that of the substrate (180 HV), and the average microhardness of sintered samples is 925.5 HV.  Figure 11 shows the relationship curves between the wear weight-loss and wear time with different RE content and sintered samples. The wear weight-loss of claddings with 0% and 2% RE content have a tendency to gradually increase and the former is significantly higher than the latter. This is because the addition of rare-earth elements forms the more ternary borides Mo2FeB2, which serves as a wear-resistant framework and effectively ensures the wear resistance of the deposited metal. At the same time, there is enough Fe-based solid solution in the cladding, which guarantees sufficient hardness in the material with certain toughness. The advantages of the two sides are fully combined to improve the wear resistance of the cladding. However, when the RE content is 0%, the amount of ternary boride Mo2FeB2 is insufficient (the area fraction of is 59%) and the grain size of Mo2FeB2 hard phase is relatively coarse (the grain size of is 16.52 μm). Thus, the increase of wear weight-loss is larger as wear progresses. When the RE content is 8%, although there is enough ternary boride as wear-resistant framework, an excessive amount of ternary boride Mo2FeB2 formed (the area fraction of is 74%) and part of the Mo2FeB2 hard phases adhered and segregated with each other as well as in a heterogeneous distribution (Figure 3d), which easily caused Mo2FeB2 hard phases to fall off during the wear process and aggravated the wear process in turn. Compared with the cladding with 0% and 8% RE content, sufficient ternary boride Mo2FeB2 (the area fraction of is 72%) is finely and uniformly distributed in the cladding (the average grain size is 4.78 μm) when the RE content is 2%, thereby showing excellent wear resistance (2.4 mg). Figure 11b shows the comparison of the wear weight-loss between the sintered sample and cladding with 2% RE content. The wear weight-loss of the sintered sample is 1.6 mg after 60 min while the counterpart of cladding with 2% RE content is 2.4 mg, which is about 70% of the wear resistance of the sintered sample.  Figure 11 shows the relationship curves between the wear weight-loss and wear time with different RE content and sintered samples. The wear weight-loss of claddings with 0% and 2% RE content have a tendency to gradually increase and the former is significantly higher than the latter. This is because the addition of rare-earth elements forms the more ternary borides Mo 2 FeB 2 , which serves as a wear-resistant framework and effectively ensures the wear resistance of the deposited metal. At the same time, there is enough Fe-based solid solution in the cladding, which guarantees sufficient hardness in the material with certain toughness. The advantages of the two sides are fully combined to improve the wear resistance of the cladding. However, when the RE content is 0%, the amount of ternary boride Mo 2 FeB 2 is insufficient (the area fraction of is 59%) and the grain size of Mo 2 FeB 2 hard phase is relatively coarse (the grain size of is 16.52 µm). Thus, the increase of wear weight-loss is larger as wear progresses. When the RE content is 8%, although there is enough ternary boride as wear-resistant framework, an excessive amount of ternary boride Mo 2 FeB 2 formed (the area fraction of is 74%) and part of the Mo 2 FeB 2 hard phases adhered and segregated with each other as well as in a heterogeneous distribution (Figure 3d), which easily caused Mo 2 FeB 2 hard phases to fall off during the wear process and aggravated the wear process in turn. Compared with the cladding with 0% and 8% RE content, sufficient ternary boride Mo 2 FeB 2 (the area fraction of is 72%) is finely and uniformly distributed in the cladding (the average grain size is 4.78 µm) when the RE content is 2%, thereby showing excellent wear resistance (2.4 mg). Figure 11b shows the comparison of the wear weight-loss between the sintered sample and cladding with 2% RE content. The wear weight-loss of the sintered sample is 1.6 mg after 60 min while the counterpart of cladding with 2% RE content is 2.4 mg, which is about 70% of the wear resistance of the sintered sample.  Figure 12 shows the wear surface morphologies of the sintered sample and the claddings with 0%, 2% as well as 8% RE content for 60 min. From Figure 12a, there apparently exists wear debris on the wear surface, this is because the average grain size of the Mo2FeB2 phases is larger (16.52 μm) and the average free path of the matrix is also larger, which makes the matrix spacing between ternary borides increase and the abrasive particles are easily able to damage the matrix to form wear debris. When the RE content is 2% (Figure 12b), there is some adherent metal next to the hard phases. Research shows that adding proper rare-earth Y elements to the deposited metal can refine the structure and improve the toughness. Under the condition of multiple-impact wear, the plastic deformation occurs to the wear surface, which delays the crushing process and improves the wear resistance [34]. Therefore, the Mo2FeB2 phase is finely and uniformly distributed in the cladding when the RE content is 2%, the spacing between Mo2FeB2 becomes smaller, that is, the average free path of the matrix is smaller and the boride prevents the abrasive particles from damaging the matrix, which makes the wear resistance of cladding improved. At the same time, the boride and the matrix structure are mutually protected and Mo2FeB2 functions as wear-resistant framework. However, when the RE content reaches 8% (Figure 12c), there are too many Mo2FeB2 phases and some of them are connected to each other (Figure 3d), which reduces the fluidity of the liquid molten pool. Although the average free path of the matrix is small, the boride and the matrix structure cannot mutually protect due to the absence of the Fe-based solid solution. The bonding strength between hard phases and the matrix is reduced, Mo2FeB2 phases drop down during the wear process and the fallen hard phases become abrasive to aggravate the wear, which corresponds to results of the wear weight-loss ( Figure 10). As for the sintering sample (Figure 12d), whose wear morphology is similar to the cladding with 2% RE content, only a small amount of plastic deformation appears on the wear surface.  Figure 12 shows the wear surface morphologies of the sintered sample and the claddings with 0%, 2% as well as 8% RE content for 60 min. From Figure 12a, there apparently exists wear debris on the wear surface, this is because the average grain size of the Mo 2 FeB 2 phases is larger (16.52 µm) and the average free path of the matrix is also larger, which makes the matrix spacing between ternary borides increase and the abrasive particles are easily able to damage the matrix to form wear debris. When the RE content is 2% (Figure 12b), there is some adherent metal next to the hard phases. Research shows that adding proper rare-earth Y elements to the deposited metal can refine the structure and improve the toughness. Under the condition of multiple-impact wear, the plastic deformation occurs to the wear surface, which delays the crushing process and improves the wear resistance [34]. Therefore, the Mo 2 FeB 2 phase is finely and uniformly distributed in the cladding when the RE content is 2%, the spacing between Mo 2 FeB 2 becomes smaller, that is, the average free path of the matrix is smaller and the boride prevents the abrasive particles from damaging the matrix, which makes the wear resistance of cladding improved. At the same time, the boride and the matrix structure are mutually protected and Mo 2 FeB 2 functions as wear-resistant framework. However, when the RE content reaches 8% (Figure 12c), there are too many Mo 2 FeB 2 phases and some of them are connected to each other (Figure 3d), which reduces the fluidity of the liquid molten pool. Although the average free path of the matrix is small, the boride and the matrix structure cannot mutually protect due to the absence of the Fe-based solid solution. The bonding strength between hard phases and the matrix is reduced, Mo 2 FeB 2 phases drop down during the wear process and the fallen hard phases become abrasive to aggravate the wear, which corresponds to results of the wear weight-loss ( Figure 10). As for the sintering sample (Figure 12d), whose wear morphology is similar to the cladding with 2% RE content, only a small amount of plastic deformation appears on the wear surface.